Thermoplastic compositions



United States Patent US. Cl. 260-876 7 Claims ABSTRACT OF THE DISCLOSURE Graft copolymers comprising a substrate of a diene rubber and a superstrate containing a high proportion of copolymerized acrylontirile together with an ester of acrylic or methacrylic acid. The graft copolymers are useful in blends of acrylonitrile copolymers.

This is a division of our prior US. patent application, Ser. No. 539,738, filed Apr. 4, 1966.

This invention relates to thermoplastic compositions derived from a diene rubber and a resin, and to the production of shaped articles therefrom.

In particular, it relates to graft copolymers comprising a substrate of a diene rubber and a superstrate containing a high proportion of copolymerized acrylonitrile, and to blends of such graft copolymers with polymers containing a high proportion of acrylonitrile units. The products of the invention are tough and at the same time rigid and unusually hard.

The superstrate contains a high proportion of acrylonitrile with an ester of acrylic or methacrylic acid and optionally an N-aryl maleimide which may provide at least 1% molar of the units in the superstrate. Arornatically conjugated monomers such as styrene and amethylstyrene are excluded from the superstrate owing to their normally inhomogeneous copolymerization with acrylontirile. Rubber-free resins from the superstrate monomers are exceptionally strong materials with high softening points, but they are insufiiciently tough for many purposes.

The superstrate contains from 45% to 90% (preferably 60% to 84%) molar of units from acrylonitrile, from to 20% (preferably not more than molar of units from at least one N-aryl maleimide, and from 5% to 35% (preferably to molar of units from said ester of acrylic or methacrylic acid.

The N-aryl maleimides are conveniently obtained from anilines (primary arylamines). Many different anilines are readily available and yield N-aryl maleimides that may be used as comonomers for the copolymers. The aryl substituent is derived from an aromatic hydrocarbon or heterocycle in which one or more of the hydrogen atoms may be replaced by other atoms or groups. Substituents containing active hydrogen atoms, however, are generally to be avoided because they may interfere with polymerizations catalysed by free radicals. The aryl groups that may be present in the Naryl maleimides include, for example phenyl, 4-diphenyl, l-naphthyl, all the monoand di-methylphenyl isomers, 2,6-diethy1phenyl, 2-, 3- and 4- chlorophenyl, 4-bromophenyl and other monoand dihalophenyl isomers, 2,4,6-trichlorophenyl, 2,4,6-tribromophenyl, 4-n-butylphenyl, 2-methyl-4-n-butylphenyl, 4- benzylphenyl, 2-, 3- and 4-methoxyphenyl, 2-, 3- and 4- ethoxyphenyl, 2,5-diethoxyphenyl, 4-phenoxyphenyl, 4- methoxycarbonylphenyl, 4-cyanophenyl, 2-, 3- and 4- 3,549,725 Patented Dec. 22, 1970 ice nitrophenyl and methylchlorophenyl (2,3-, 2,4-, 2,5- and 4,3-isomers). The N-(o-substituted phenyl) maleimides are generally less colored than the other isomers or the unsubstituted compounds and may therefore be preferred if a relatively colorless product is desired.

The other ethylenically unsaturated monomer is an ester of acrylic acid or methacrylic acid such as methyl, ethyl, n-butyl and 2-ethylhexyl acrylates and methyl and n-butyl methacrylates.

The diene rubber in the substrate contains from 40% to 100% molar of at least one conjugated 1,3-diene monomer and from 0% to 60% of at least one other ethylenically unsaturated monomer copolymerizable with free-radical catalysts. Suitable dienzes include for example, butadiene, isoprene, 2,3-dimethylbutadiene, piperylene and chloroprene. As comonomers acrylonitrile and styrene are particularly convenient, although a wide variety of other monomers may be used, including many of those listed above as examples of ethylenically unsaturated comonomers for the superstrate herein and in Ser. No. 539,738, the disclosure of which is. incorporated herein by reference. Diene homopolymers (e.g. polybutadiene) and copolymers with a low proportion of comonomer have lower glass transition temperatures and may therefore be preferable especially when the product is required for service at low temperatures.

The compositions of the invention can be produced by a process comprising sequential polymerization. In this process, the monomers for the superstrate are polymerized by free-radical catalysis in the presence of the diene rubber. The process is carried out using the appropriate techniques for polymerizations catalyzed by free radicals, conveniently in bulk or in aqueous suspension or emulsion. A similar emulsion process or a stereospecific process may be used to make the diene rubber. The graft copolymer may then be employed as a latex or isolated from the polymerization medium, freed from residual monomers, and dried. The product of this sequential polymerization may be blended if desired with a resin, e.g. a resin formed from the superstrate monomers as described herein or in Ser. No. 539,738, the disclosure of which is incorporated herein by reference. This blending step can be used to produce tough and strong compositions. The grafts are therefore, according to the invention, useful materials for blending with resins to give tough compositions. The resin used for blending is not necessarily one made from the same monomers as the grafted portion but can be any resin of adequate strength especially one having a high content of nitrile groups. This may be for example a copolymer of acrylonitrile (45% to molar, preferably 60% to 84% molar) with at least one other copolymerizable ethylenically unsaturated monomer, e.g. a homogeneous copolymer with a conjugated aromatic olefine.

A product in many ways equivalent to such a blend may also be obtained directly by adjusting the conditions of the grafting polymerization so that some of the superstrate monomers copolymerize to give some separate resin as well as the graft.

The resultant products are thus composed at least partially of the type of material usually referred to as graft copolymer. It is possible, however, that the superstrate in the grafted material is not all chemically bonded to the rubber but contains resin from the superstrate monomers associated with the rubber in a much more intimate physical mixture than can normally be obtained by blending preformed polymers.

The amount of rubber in the final blend is not the only factor governing toughness, which depends also on the amount of resin grafted onto the rubber in the graft used for blending.

Preferably the blend comprises from 1% to 50% by weight of the diene rubber. Compositions containing below 25% of the rubber are particularly hard scratch-resistant materials with high impact strength, and while there is an apparently smooth transition of properties the compositions containing at least 20% (preferably not more than 40%) of the rubber tend to be hard materials with very high impact strength.

Preferred blends according to the invention, unlike some rubber/resin blends, show no apparent separation of phase on warming from 180 C. to +20 C.

The compositions of the invention, mixed with any desired fillers or reinforcing materials, lubricants and stabilizers, can be used as thermoplastic raw materials to make articles which require a good resistance to impact. Their toughness coupled with high strength and high softening point may thus be displayed to advantage. For example, the compositions may be extruded into sheet or tube, and the sheet can be calendered with embossing if desired or can be shaped as required, e.g. by pressing drawing or vacuum-forming. The compositions can also be compression-molded and injection-molded. Examples of articles that may thus be produced using the compositions of the invention include panelling and exterior casing for machinery (as in motor cars, office machines and household equipment), crash helmets, pipes for conveying fluids, and telephone receivers. The use of compositions of the invention having superior tensile strength coupled with rigidity and toughness may allow economy of material in comparison with currently used products in that thinner pieces would serve the same purpose. The advantageous physical properties of the compositions may also permit them to be used in engineering applications for which plastics have not hitherto been suitable.

The toughness of a material such as a thermoplastic polymer is connected with the amount of energy that the material is capable of absorbing without breaking when stressed in tension, and this in turn is related to the way in which the material behaves when stressed in tension at different temperatures. When an increasing uniaxial tensile stress is applied an any one temperature, the material will eventually either break or yield. The material breaks before yielding if it is brittle, and whether or not it is brittle depends on the temperature. There is a temperature (the brittle point) peculiar to any particular material above which it eventually yields under tensile stress and below which it undergoes brittle fracture. At temperatures below the brittle point, the amount of energy the material can absorb when stressed in tension is low and varies little with temperature. Above the brittle point, however, the amount of energy that can be absorbed rises steeply as the temperature increases. To be tough at room temperature, therefore, a material should have a relatively low brittle point.

The brittle points of two different materials can be compared indirectly by comparing their properties under stress, first at a low temperature where both materials are brittle, and secondly at a higher temperature where neither material is brittle. Convenient temperatures for these tests are obtained by using liquid nitrogen (the sample being at about 180 C.) and room temperature (+20" C.) respectively. Up to its brittle point, the stress at which a material breaks falls only slightly as the temperature increases. Above the brittle point, however, the stress at which the material yield falls relatively steeply as the rise of temperature continues. Consider therefore two materials which break at the same stress at 180 C. but have different brittle points. The material with the lower brittle point (the tougher material) will yield at the lower stress at +20 C. Conversely, the tougher of two different materials yielding at the same stress at +20 C. will be the one which breaks at the higher stress at 180 C.

In order to toughen a material, therefore, it is desirable to alter its composition so as to preserve a high resistance 4 to brittle fracture at 180 C. but reduce the stress at which it yields at +20 C.

Resins containing a high proportion of homogeneously copolymerized acrylonitrile have unusually high breaking stresses at -l C. and high yielding stresses at +20 C. According to the invention it has been found that graft copolymers and their blends may be produced so as largely to retain the high breaking stress at C. but having a reduced yielding stress at +20 C. Owing to the high breaking stress at 180 C., the yielding stress at +20 C. can be reduced sufficiently for the product to become tough while remaining adequately rigid and hard. The invention accordingly provides materials which have a good resistance to impact coupled with excellent structural properties.

The breaking stress at 180 C. was measured on specimens 51 mm. long and 12.7 mm. wide milled from a compression-molded sheet 3 mm. thick. The specimen rested on two supports 38.1 mm. apart and midway between them a load was applied sufiicient to bend the specimen at the rate of 457 mm./min. The breaking stress was calculated by multiplying the load at the moment of rupture by the factor:

The yielding stress at +20 C. was measured on specimens 76 mm. long and 14 mm. wide milled from a compression-molded sheet 3 mm. thick. The cross-sectional area across the center of the specimen was reduced to 9 mm. by milling two slots (radius of curvature 31 mm.) opposite each other in the long edges so that the narrowest width of the specimen was 3 mm. A tensile stress was then applied to the specimen sufficient to elongate it at the rate of 12.7 mm./min. and the stress at the yield point was recorded.

For comparison with the data of the examples below, the flexural breaking stress at -180 C. of the rubber-free resins formed from the superstrate monomers is usually about 25 kg./mm. and the tensile yielding stress is usually about 11 kg./mm. The compositions of the invention often largely retain the high breaking stress at l80 C. characteristic of the resins but have improved toughness (as may be indicated by the greatly reduced yielding stress).

As explained above, a useful indication of the relative toughness of materials is often given by comparing their flexural breaking stresses at 180 C. and their tensile yielding stresses at +20 C. With materials that are so tough as not to be brittle in the tensile test at -40 C., however, this approach loses some of its value. An additional test (the notched specimen impact test) has therefore been used to supplement the comparative measurements on such materials.

In this test, a specimen 60 mm. long, 6.5 mm. wide and 3 mm. thick was given a 45 notch 2.8 mm. deep (tip radius not more than 0.25 mm.) in the center of one edge. It was supported between two supports 50 mm. apart and struck centrally on the edge opposite the notch by a pendulum dropping from 30 cm. with more than sufficient energy to break the specimen. From the residual energy of the pendulum the energy required to break the specimen was calculated and divided by the cross-sectional area of the specimen at the notch. The resulting value (expressed in joules/cm?) represented the energy required to cause cracks to propagate in the material.

Using this test at room temperature (2026 C.), various ABS materials broke at 0.5 j./cm. or somewhat above. Compositions of the invention have been found to have similar toughness in this test; for example the products of Example 2 broke at 0.44 j./cm. Thus compositions of the invention possess toughness in combination with exceptionally high tensile strength.

The following examples illustrate the invention. Breaking stress, yielding stress, and toughness were measured as described above. Measurements were made at +20 C. (room temperature) unless otherwise indicated.

EXAMPLE 1 Acrylonitrile (75% molar), N-phenylmaleimide (5% molar) and isobutene (20% molar) monomers were co- 6 gave a transparent and very pale yellow plaque. This had full and one-tenth Vicat softening points of 95 C. and 85 C. respectively, a breaking stress at -180 C. of 23.3 kg./mm. and a melt viscosity of 21 kP. at 260 C. and

polymerized in the presence of a rubber latex, not short- 5 a shear rate of 1000/84 stopped, formed of 30% molar acrylonitrile and 70% XA 4 molar butadiene andcontaining 49.4% solids of which 77% was insoluble in methyl ethyl ketone A rubber graft for blending with a separately pre- The latex (5585 was brought to pH with 01 N pared resin was made by copolymerizing acrylonitrile sulphuric acid and placed in a shaking autoclave. A solu- 10 (75% molar) N-phenylmalelmlde molar) and tion f N pheny]ma1eimide (1425 g) in acrylonitrfle isobutene (20% molar) 1n the presence of a rubber latex (653 was added, together with water (650 cms) potas not short-stopped formed of 30% molar acrylonitrile and slum persulphate (1.55 g.) and sodium metabisulphite 70% molar butadlene and conlammg 475% solids- (1.03 g.). The contents of the autoclave were repeatedly latex (1475 was adlusted to P Placed pressurized to 7 kg./cm. with nitrogen and vented. Isowith Walter (680 i F liersulphale (1'40 butene (18.8 g.) was then added and the reaction mixture and Sodlum metablsulphlte (1308 In shaking was maintained at for 18 hours under nitrogen at autoclave, Which was then thrice pressurized to 7 kg./cm. 7 kg./cm. The solid composition (97.1 g.) was isolated wlth mtroge? vented- Nphenylmalelmide (10-1 by adding an aqueous solution (10 cm?) of calcium chloand acrylonltflle were added and t ride saturated at room temperature, washing the solid six 20 Clave was aganthr 1Ce pressunzed to 7 wlth Intro times with water at 90 C. and then with cold methanol, gen and vented' Fmauy lsobutene (21-9 cm-a) was added and drying under Vacuum at .0 0 Assuming that the and the autoclave was shaken at 30 C. for 18 hours product comprised all the rubber initially employed, it mtrogen ?bout 4 P"- The Product was a Contained 284% rubber and 20% butadiene' The n white latex containing 13.5% solids of wh1ch about 58% Vicat and one-tenth Vicat softening points of the material was P were c and c respectively This product was blended with a latex of a homo- On compressiommolding the composition gave a clear geneously copolymerlzed copolymer of acrylonitrile (78% yellow plaque. Its breaking stress at --180 C. and yieldmolar) and Styrene (22% molar) blends were ing stress at 0 were mspgctively 25 z and coagulated to give strong tough compositions. Their prop- 5.9 kg./mm. Similar measurements on commercially ertles are tabulated belowavailable acrylonitrile/butadiene/styrene terpolymers and blends (ABS materials) showed breaking stresses at gi ig f l g figffi 2 g 180 C. of 13 to 17 kg./mm. and yielding stresses at Tpu hnessj./cm. IIIIIIIIIII 0:4 312 0 of 3.2m kg/mma 3sra asrsagmd. .0. The melt viscosity of the composition was 12.5 kP. at Mo, degr ees eenti radeQIllIIlI 100 as 260 C., measured at a shear rate of 1000/ s. The extrudate was transparent and pale yellow and the melt viscosity X M 5 remained unchanged over five mlnutes at 260 C. The process described in Example 4 was repeated, cept that methyl acrylate (22.7 ems; 20% molar) was EXAMPLE 2 used instead of isobutene and was added to the autoclave he other monomers. The roduct was a latex con- Acrylon1tr1le(75% molar), N-2-chloro hen lmaleimide i t p (5% molar) and methyl acrylate (20% m blarg monomers lammg 163% Sohds of wh1ch about was p T were copolymerized in the presence of a rubber latex, not Isolated graft hadofun and on'tenth Vicat .sofl.enlng polms short-stopped, formed of 32% molar acrylonitrile and 32 8 78 respectlvely and a yleldmg stress of 68% molar butadiene and containing 48.4% solids, as m described in Example The product was blended as a latex with a latex of an The latex (5706 g; 276 Solids) was brought to PH acrylonitrlle/styrene copolymer as in Example 4 and the 5.7. Acrylonitrile (65.8 g.), N-2-chlorophenyl maleimide f l coagulated to f Strong tough composmon (171 g.) and methyl acrylate (2855 was added taming 25% rubber having full and one-tenth Vicat softgether with sodium metabisulphite (0.33 g.), potassium .enmg pomts of 104 i 93 respecblvely yleld' persulphate (0.5 g.) and water (650 cm. The polymerizamg s.tress 9 a togghness m the notched tion was conducted as described in Example 1 for 21 hours speclmen Impact test of at 30: C. to yield 112 g. solids. The isolated composition H EXAMPLE 6 contained 24.7% rubber and 16.9% butadiene. 0n com- 00 pression-molding at 200 C. it gave a transparent pale |Rubber grafts were prepared by the process described yellow plaque. This had a breaking stress at -180 C. of in Example 4, using the quantities of rubber and mono- 23.2 kg./mm. a yielding stress at +20 C. of 7.2 kg./ mers tabulated below.

Starting materials:

Rubber, g 240 166 180 339 140 106 Acrylonitrile,g 72.3 72.3 147.0 224 224 224 N-phenylmaleimide, g 15.7 15.7 30.3 45.4 45.4 45.4 Isobutene,g-. 20.4 20.4 42.3 03.5 63.4 63.5 Water, cm. 2,400 1,700 2,040 2, 500 2, 300 2, 500 Nazszoa, g 1.30 1. 30 4.0 6.0 6.0 6.0 Kzszog,g 2.16 2.16 4.4 6.6 6.6 0.0 Properties of the isolated grafts:

Percent rubber 91 74 66 53 35 29 Breaking stress, kg./n1m. 0. 3 0.5 1. 6 Yielding stress, kgJmm." 2.4 4.1 5.0

mm. and a melt viscosity of 20 kP. at 260 C. and a shear rate of 1000/ s.

EXAMPLE 3 The process described in Example 2 was repeated using 76.5 g. of the latex (37 g. solids). The solid composition (124.2 g.) when isolated contained 29.8% rubber and These grafts as latices were blended with the latex of a resin made by a process generally similar to that of Example 4 (but omitting the rubber) from acrylonitrile (1750 cm. N-penylmaleimide (304.5 g.), isobutene (655 cm. sodium metabisulphite (10.37 g.), ammonium persulphate (12.5 g.), sodium dodecyl sulphate (12.25 g.)

20.4% butadiene. On compression-molding at 200 C. it and octanethiol (5.6 ems). This resin when isolated had Rubber in graft by weight, per

cent Yielding stress, kg./mm Toughness, j./cm.

Outstanding toughness is shown by the blend made with the graft containing 53% of rubber.

EXAMPLE 7 A rubber graft for blending with a separately prepared resin Was made by copolymerizing acrylonitrile (80% molar) and methyl acrylate (20% molar) in the presence of a rubber latex not short-stopped formed from 30% molar acrylonitrile and 70% molar butadiene and containing 47.5% solids.

The latex (126.4 g.) was adjusted to pH 5.7 and placed with Water (600 cm. ammonium persulphate (1.20 g.) and sodium metabisulphite (0.99 g.) in a one-liter shaking autoclave, which was then thrice pressurized to 7 kg./cm. with nitrogen and vented. Acrylonitrile (53.0 cm?) and methyl acrylate (18.1 cm?) were added, and the autoclave was again thrice pressurized to 7 kg./cm. with nitrogen and vented. The autoclave was shaken at 30 C. for 16 hours under nitrogen at about 1.6 kg./cm. The product contained 61% of rubber.

A sample of the graft latex was coagulated using 0.75% aqueous calcium chloride to give a polymer which was washed twice with water and twice with methanol and dried and then gave transparent yellow moldings at 200 C.; full Vicat softening point 65 C.; toughness 1.63 j./cm.

The graft latex was blended with the latex of a resin made by a process generally similar to that of Example molar), N-phenylmaleimide (5% molar) and methyl acrylate (20% molar). The amount of the resin latex added was such that the resulting blend contained of rubber. The product was isolated using 0.75% aqueous calcium chloride and washed and dried. It gave transparent yellow moldings at 200 C.: full Vicat softening point 94 C.; yielding stress 8.3 kg./mm. toughness 2.10 j./cm.

EXAMPLE 8 A rubber graft for blending with a separately prepared resin was made by copolymerizing acrylonitrile (75% molar), N-phenylmaleimide (5 molar) and methyl acrylate (20% molar) in the presence of a polybutadiene latex containing 39.5% solids.

The latex (177.2 g.) was placed with water (680 cm?) and ammonium persulphate (1.40 g.) in a one-liter shaking autoclave which was then thrice pressurized to 7 kg./cm. with nitrorgen and vented. Acrylonitrile (61.5 cm. N-phenylmaleimide (10.1 g.) and methyl acrylate (22.7 cm?) were added and the autoclave was again thrice pressurized to 7 kg./cm. with nitrogen and vented. The autoclave was shaken at 60 C. for 17 hours under nitrogen at 1.0 to 1.8 kg./cm. The resulting latex contained 15.7% solids of which 47% was rubber.

A sample of the graft isolated as in Example 7 gave transparent brown moldings at 200 C.: full and onetenth Vicat softening points 89 C. and 78 C. respectively; yielding stress 2.0 kg./mm.

The graft latex was blended with the latex of an acrylonitrile/N-phenylmaleimide/methyl acrylate resin as described in Example 7 to give blends containing 10% and 20% of rubber, which were isolated as before. Their properties are tabulated below.

Percent rubber in blend 10 20 Yielding stress, kg./nnn. 9. 1 7. 3 Toughness, j./cn1. 0.25 0. 95

EXAMPLE 9 Rubber grafts were made as described in Example 8 but using 0.5 cm. 0.96 cm. and 1.93 cm. octanethiol in the polymerization mixture. The graft latices were blended with the latex of an acrylonitrile/N-phenyL maleimide/isobutene resin as described in Example 6 to give products containing 10% and 20% of rubber. The properties of the grafts and blends, isolated as before, are tabulated below.

Oetanethiol used, cm. 0.5 0 96 1.93 Grafts:

Full Vicat softening point, degrees centigrade. 93 96 91 A0 Vicat softening point, degrees centigrade. 83 80 Yielding stress, kg./rnm. 3. 1 3. 1 2.8 Percent of rubber by weight 48 48 48 Blends containing 10% of rubber:

Yielding stress, kgJmm. 10. 0 10.0 9. 5 'Ioughr1.%sj./cm. 0.14 0.07 0.16 Blends containing 20% of rubber Yielding stress, kg./mm. 8.1 8.0 7. 7 T0ughnessj./cm. 0.61 0 63 0.67

EXAMPLE 10 A polybutadiene latex (184 g.; 70 g. solids), water (650 cmfi), ammonium persulphate (1.4 g.), acrylonitrile (79.9 cm.; 1.2 mole) and methyl acrylate (27.1 emf; 0.3 mole) were polymerized under nitrogen in a one-liter shaking autoclave for 16 hours at 80 C. The resulting graft latex contained 16.6% solids of which 45.7% was rubber. This was latex-blended with a homogeneously copolymerized acrylonitrile/ styrene latex (molar ratio 78:22, reduced viscosity 0.86 at 0.5% in dimethylformamide at 25 C.) to give a tough strong blend containing 20% of rubber.

What is claimed is:

1. A graft copolymer comprising (i) a substrate of a diene rubber containing 40% to 100% molar of at least one conjugated 1,3-diene monomer and from 0% to 60% molar of at least one other ethylenically unsaturated monomer copolymerizable therewith using free radical catalysts and (ii) a superstate which contains from 45% to molar of units from acrylonitrile, from 1% to 20% molar of units from at least one N-aryl maleimide and from 5% to 35% molar of units from at least one ester selected from the esters of acrylic and methacrylic acids.

2. A graft copolymer according to claim 1 in which the superstrate contains from 60% to 84% molar of units from acrylonitrile.

3. A graft copolymer according to claim 1 in which the superstrate contains from 1% to 10% molar of units from N-aryl maleimide.

4. A graft copolymer according to claim 1 in which the superstrate contains from 15% to 30% molar of units from the esters selected from the esters of acrylic and methacrylic acids.

5. A graft copolymer according to claim 1 in which the diene rubber substrate is polybutadiene.

6. A blend of a graft copolymer according to claim 2 and a resin containing 60% to 84% molar of units from acrylonitrile, 40% to 16% molar of units from at least one ethylenically unsaturated comonomer selected alkenes, dienes, esters of acrylic and methacrylic acids, vinyl esters, vinyl ethers, esters of fumaric acid, unsaturated nitriles, vinyl chloride, vinylidene chloride and achloroacrylonitrile, and 0% to 20% molar of units from at least one N-aryl maleimide, the blend containing from 1% to 50% by weight of rubber.

7. A blend of a graft copolymer according to claim 2 and a homogeneously copolymerized resin containing 9 60% to 84% molar of units from acrylonitrile, 40% to 16% molar of units from at least one conjugated aromatic olefine, and 0% to 20% molar of units from at least one N-aryl maleimide, the blend containing from 1% to 50% by weight of rubber.

3,262,993 7/1966 Hagemeyer et a1. 260-879 8/1966 Osmond 260--879 10 10 3,265,708 8/1966 Stiteler 260-879 3,322,852 5/ 1967 Trementozzi et al. 260879 3,352,832 11/1967 Barr et a1. 260-78U 5 MURRAY TILLMAN, Primary Examiner H. ROBERTS, Assistant Examiner US. Cl. X.R. 26029.7, 78, 879 

